CN103866165A - Isotropical high-strength high-toughness particle reinforced aluminium-based composite material and preparation method thereof - Google Patents
Isotropical high-strength high-toughness particle reinforced aluminium-based composite material and preparation method thereof Download PDFInfo
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Abstract
The invention relates to isotropical high-strength high-toughness particle reinforced aluminium-based composite material and a preparation method thereof. In the composite material, the granularity of reinforced particles is 1-25 mu m, the volume percentage is 5%-30%, the reinforced particles are dispersed and distributed in a substrate in the aspect of space, and the reinforced particles and the substrate form high-strength interface combination. The preparation method comprises adding the reinforced particles and aluminium alloy powder into a material mixing barrel for mechanical mixing, so as to obtain a composite material, then performing vacuum hot pressing on the composite material to form preform bodies, and successively performing extrusion, forging and rolling on the preform bodies for deformation. The prepared composite material can be used as bearing members with complex stress in the aerospace field. The product is characterized in that the material has excellent properties such as isotropical property, high strength, high toughness and the like, and is stable in quality, low in cost, easy for large-scale industrial production, and the like.
Description
Technical field
The invention belongs to particle enhanced aluminum-based composite material technical field; Be particularly related to isotropy and high-strength and high ductility particle enhanced aluminum-based composite material preparation method.
Background technology
Compared with matrix alloy, particle enhanced aluminum-based composite material has the excellent over-all propertieies such as high specific strength, high specific stiffness, thermal expansivity are little, good heat conductivity, has started and has progressively been widely used in aerospace field.Since the eighties in last century, China has in succession dropped into a large amount of man power and materials and has carried out research and the application and development of such matrix material, attempt in important application occasions such as aerospace, adopt the particle enhanced aluminum-based composite material of lightweight to replace traditional aluminium alloy and titanium alloy as structured material, so that realize the lightweight of component.Therefore, particle enhanced aluminum-based composite material must possess low density, high-modulus and good toughness plasticity.
At present, the preparation method of particle enhanced aluminum-based composite material mainly contains four kinds: powder metallurgic method, stirring casting method, spray deposition and pressure casting method.Wherein powder metallurgic method is the most ripe, the accurately effective content of regulation and control reinforcement particle, and also it is controlled to realize Fine Texture of Material, obtains the material with high-strength and high ductility and stable performance.
Due to adding of ceramic reinforcement, the plasticity of particle enhanced aluminum-based composite material is poor, must reinforcement uniform particles be distributed in aluminum substrate by viscous deformation, and improve the interface combination of reinforcement-matrix, to increase substantially the plasticity of material, realize the object of high-strength and high ductility, reach the basic application indexes (unit elongation >5%) of space flight and aviation structural part.Although through traditional viscous deformation means, as extruding, forging and rolling etc., can significantly improve intensity and the plasticity of particle enhanced aluminum-based composite material, but also can strengthen the anisotropy of material internal simultaneously, such as: will be apparently higher than perpendicular to the direction of extrusion along the mechanical property of the direction of extrusion, the physicals of both direction also has certain difference; Along forge radially or the mechanical property of rolling direction all higher, these differences are mobile relevant in plastic history with material all.In aerospace field, for the structural part of real service state lower stress complexity, the anisotropy of this material can greatly shorten its fatigue lifetime, has seriously hindered the development and application of particle enhanced aluminum-based composite material on such structural part.Therefore the particle enhanced aluminum-based composite material that, how to obtain interior tissue and performance isotropy, high-strength and high ductility seems particularly important.
Summary of the invention
Object of the present invention is just to realize a kind of isotropy and high-strength and high ductility particle enhanced aluminum-based composite material.
Another object of the present invention is to realize being suitable for a kind of process stabilizing of above-mentioned isotropy and high-strength and high ductility particle enhanced aluminum-based composite material and preparation method cheaply, by two kinds of different viscous deformation modes, making the distribution of reinforcement particle in aluminum substrate arrive space uniform distributes, between reinforcement and matrix, form good interface simultaneously and be combined, to prepare isotropy and high-strength and high ductility particle enhanced aluminum-based composite material.
To achieve these goals, the present invention takes following technical scheme:
Isotropy of the present invention and high-strength and high ductility particle enhanced aluminum-based composite material are made up of reinforcement particle and alloy matrix aluminum.
Reinforcement particle spatially disperse is uniformly distributed in alloy matrix aluminum, and forms high-intensity interface with matrix and be combined;
The size range of reinforcement particle is 1 ~ 25 μ m;
And the volume percent in matrix material is 5% ~ 30%;
The size range of Al alloy powder is 5 ~ 60 μ m.
Described reinforcement particle is the Al with features such as high rigidity, high elastic coefficient, high strength and low density
2o
3any one in (aluminum oxide), SiC (silicon carbide) and AlN (aluminium nitride); Alloy matrix aluminum is any one alloy in duralumin (2 × × ×).
This isotropy and high-strength and high ductility particle enhanced aluminum-based composite material are that the processing mode manufacture that adopts reinforcement particle and Al alloy powder batch mixing, vacuum hotpressing to be configured as billet, is hot extruded into bar and high temperature forging or hot rolling forms.
A kind of preparation method who manufactures particle enhanced aluminum-based composite material of the present invention, the method comprises the steps:
(1) matrix alloy of the reinforcement particle that is 5 ~ 30% by the volumn concentration in reinforcement particle in matrix material and volumn concentration 70 ~ 95%, calculates the two required weight separately;
(2) required reinforcement particle, Al alloy powder and steel ball are joined in the mixing machine of standard machinery mixer, carry out mechanical batch mixing;
(3) composite powder making is packed in No. 45 steel die, then vacuum hotpressing is configured as billet, and hot pressing temperature is 600 ~ 650 ℃, and vacuum tightness is 1 ~ 8 × 10
-3pa, pressure is 50 ~ 100MPa;
(4) matrix material hot pressing billet is carried out to hot extrusion, extrusion temperature is 400 ~ 450 ℃, and extrusion ratio is 10 ~ 20:1, and extrusion speed is 0.1 ~ 5mm/s;
(5) matrix material extruded bars is divided into the bar that length is 500 ~ 1200mm, partition tools can adopt Wire EDM, band saw or disc saw;
(6) the matrix material bar that is 500 ~ 1200mm by length carries out high temperature forging or hot rolling, forging or rolling temperature are 400 ~ 450 ℃, total deformation >60%, single pass heavy deformation should be <45%, every time need carry out the high temperature anneal, and annealing process is: 400 ~ 450 ℃ of insulation 2 ~ 4h.
The distributing homogeneity of reinforcement particle in aluminum substrate is one of important factor affecting composite material strength and plasticity, the reunion in aluminum substrate of reinforcement particle causes the decline of the strength of materials and plasticity, therefore, improving reinforcement even particle distribution is to prepare one of high-strength and high ductility matrix material brief problem urgently to be resolved hurrily.Large quantity research shows that reinforcement particle and aluminum matrix alloy powder size proportioning can directly affect reinforcement even particle distribution.Therefore, the size range of selecting reinforcement particle is 1 ~ 25 μ m, and the size range of Al alloy powder is 5 ~ 60 μ m.
In above-mentioned steps (2), steel ball used is take high-carbon steel ball as good, and steel ball size is Ф 10 ~ 15mm.
Manufacturing when particle enhanced aluminum-based composite material, first press the volumn concentration of reinforcement particle and matrix alloy in matrix material, calculate the two required weight separately.Then reinforcement particle, Al alloy powder and steel ball are joined in mixing machine, carry out mechanical batch mixing 20 ~ 30h, ball material weight ratio is 1:1, and mixer rotating speed is 25 ~ 30rpm.The composite powder vacuum hotpressing making is configured as to billet, and hot pressing temperature is 600 ~ 650 ℃, and vacuum tightness is 1 ~ 8 × 10
-3pa, pressure is 50 ~ 100MPa.
The above-mentioned matrix material hot pressing billet making is carried out to hot extrusion, and extrusion temperature is 400 ~ 450 ℃, and extrusion ratio is 10 ~ 20:1, and extrusion speed is 0.1 ~ 5mm/s.The matrix material billet plasticity of hot pressing is lower, not only can significantly improve intensity and the plasticity of matrix material, and can improve the interface bond strength of reinforcement particle and matrix through the crimp of aximal deformation value.In addition, select rational extrusion temperature and lower extrusion speed can effectively avoid extruding cracking, guarantee higher yield rate.
Use Wire EDM, band saw or disc saw that the above-mentioned matrix material extruded bars making is divided into the bar that length is 500 ~ 1200mm, then carry out high temperature forging or hot rolling, forging or rolling temperature are 400 ~ 450 ℃, total deformation >60%, single pass heavy deformation is answered <45%, every time need carry out the high temperature anneal, and annealing process is: 400 ~ 450 ℃ of insulation 2h.In order to guarantee that material does not ftracture in forging or the operation of rolling, single pass heavy deformation should not exceed 45%, and anneal can be eliminated the internal stress that material deformation produces effectively, can improve material plasticity and avoid strain cracking.And total deformation is greater than 60%, be even to eliminate the difference of bar in tissue and performance along the direction of extrusion and on perpendicular to the direction of extrusion in order to dwindle, realize material homogeneous microstructure distribution, performance isotropy spatially.
The advantage of particle enhanced aluminum-based composite material of the present invention is:
1, in particle enhanced aluminum-based composite material of the present invention, reinforcement uniform particles is distributed in matrix, reach the feature that space uniform distributes, between reinforcement and matrix, form high-intensity interface simultaneously and be combined, guaranteed that matrix material has the excellent performance such as isotropy, high-strength and high ductility.
2, preparation method's technique of the present invention is simple, and mixing time is short, and ratio of grinding media to material is low, has therefore not only shortened the production cycle, and can obtain at short notice a large amount of composite powders, for scale operation provides favourable condition.In batch mixing process, do not need to add any tensio-active agent, thereby avoid tramp material to introduce in composite powder, guaranteed the purity of matrix material.
3, particle enhanced aluminum-based composite material of the present invention, after the hot extrusion of aximal deformation value, can significantly improve intensity and the plasticity of matrix material; Again after high temperature forging or hot rolling, in the situation that keeping the strength of materials (under squeezed state along the direction of extrusion) substantially constant, can realize the mechanical property of material in all directions and reach same level, and the spatially disperse of reinforcement particle is uniformly distributed in matrix.
Below by embodiment and accompanying drawing, the present invention will be further described, but do not mean that limiting the scope of the invention.
Accompanying drawing explanation
Fig. 1 (a) is 15vol.%SiC
p/ 2009Al matrix material hot pressing billet 1
#along the metallographic microstructure photo (ZEISS-Axiovert 200MAT opticmicroscope amplifies 200 times) in hot pressing axially.
Fig. 1 (b) is 15vol.%SiC
p/ 2009Al matrix material hot pressing billet 1
#perpendicular to the metallographic microstructure photo (ZEISS-Axiovert 200MAT opticmicroscope amplifies 200 times) in hot pressing axially.
Fig. 1 (c) is 15vol.%SiC
p/ 2009Al matrix material extruded bars 2
#along the metallographic microstructure photo in the direction of extrusion (ZEISS-Axiovert 200MAT opticmicroscope amplifies 200 times).
Fig. 1 (d) is 15vol.%SiC
p/ 2009Al matrix material extruded bars 2
#perpendicular to the metallographic microstructure photo in the direction of extrusion (ZEISS-Axiovert 200MAT opticmicroscope amplifies 200 times).
Fig. 1 (e) is 15vol.%SiC
p/ 2009Al matrix material forges cake material 3
#along the metallographic microstructure photo (ZEISS-Axiovert 200MAT opticmicroscope amplifies 200 times) in forging and stamping direction.
Fig. 1 (f) is 15vol.%SiC
p/ 2009Al matrix material forges cake material 3
#perpendicular to the metallographic microstructure photo (ZEISS-Axiovert 200MAT opticmicroscope amplifies 200 times) in forging and stamping direction.
Embodiment
Embodiment 1:
The experiment material of the present embodiment is 15vol.%SiC prepared by powder metallurgic method
p/ 2009Al matrix material, SiC average particle size is 10 μ m, percent by volume is that 15%, 2009Al powdered alloy mean particle size is 40 μ m.
Its method for making is according to the volume fraction content 15% of reinforcement particle in designed matrix material and ratio of grinding media to material 1:1, take the steel ball 70kg of SiC powder 13.18kg, 2009Al powdered alloy 56.82kg and Ф 10mm, add in mechanical mixer, mix 24h, mixer rotating speed is 30rpm.Be the cylindrical billet A1# of Ф 300mm by above-mentioned gained composite powder vacuum hot pressing formation, hot pressing temperature is 620 ℃, and vacuum tightness is 2 × 10
-3pa, pressure is 80MPa.Be the bar A2# of Ф 80mm by the above-mentioned matrix material hot pressing billet hot extrusion molding making, extrusion temperature is 420 ℃, and extrusion ratio is 14:1, and extrusion speed is 1mm/s.Adopt Wire EDM that matrix material extruded bars is divided into the bar that length is 800mm.Above-mentioned bar is carried out to high temperature forging and obtain forging cake A3#, forging temperature is 420 ℃, the first reduction in pass is 32mm (pass deformation is 40%), the second reduction in pass is 20mm (pass deformation is 41.7%), total deformation is 65%, every time need carry out the high temperature anneal, and annealing process is: 420 ℃ of insulation 2h.
Embodiment 2:
The experiment material of the present embodiment is 25vol.%SiC prepared by powder metallurgic method
p/ 2009Al matrix material, SiC average particle size is 6 μ m, percent by volume is that 25%, 2009Al powdered alloy mean particle size is 30 μ m.
Its method for making is according to the volume fraction content 25% of reinforcement particle in designed matrix material and ratio of grinding media to material 1:1, take the steel ball 70kg of SiC powder 19.51kg, 2009Al powdered alloy 50.49kg and Ф 10mm, add in mechanical mixer, mix 24h, mixer rotating speed is 30rpm.Be the cylindrical billet B1# of Ф 300mm by above-mentioned gained composite powder vacuum hot pressing formation, hot pressing temperature is 620 ℃, and vacuum tightness is 2 × 10
-3pa, pressure is 80MPa.Be the bar B2# of Ф 80mm by the above-mentioned matrix material hot pressing billet hot extrusion molding making, extrusion temperature is 450 ℃, and extrusion ratio is 14:1, and extrusion speed is 0.5mm/s.Adopt Wire EDM that matrix material extruded bars is divided into the bar that length is 800mm.Above-mentioned bar is carried out to hot rolling and obtain sheet material B3#, rolling temperature is 450 ℃, after the first passage rolling, sheet metal thickness is 55mm (pass deformation is 31.3%), after the second passage rolling, sheet metal thickness is 35mm (pass deformation is 36.4%), after the 3rd passage rolling, sheet metal thickness is 26mm (pass deformation is 25.7%), total deformation is 67.5%, and every time need carry out the high temperature anneal, and annealing process is: 450 ℃ of insulation 2h.
In view of the Changing Pattern of each plastic period matrix material of examination mechanical property in difference sampling direction, according to GB GB/T 228.1-2010, the hot pressing billet in above-described embodiment 1 and 2, bar and cake material (sheet material) are carried out to room temperature tensile Mechanics Performance Testing.Specific implementation method is as follows: the hot pressing billet in above-described embodiment 1 and 2 is sampled along hot pressing direction with perpendicular to hot pressing direction, extruded bars samples along the direction of extrusion with perpendicular to the direction of extrusion, forge cake material along forging and stamping direction with perpendicular to the sampling of forging and stamping direction (B3# sheet material is along rolling direction with perpendicular to rolling direction sampling), treat sample thermal treatment (500 ℃ of solid solubility temperatures, be incubated 1 hour, hardening, natural aging 96 hours) after, carry out room temperature tensile Mechanics Performance Testing.Its mechanical experimental results is in table 1 and table 2
15vol.%SiC
pthe mechanical property of/2009Al matrix material is as shown in table 1.As can be seen from the table, the plasticity of matrix material hot pressing billet is poor, lower than the basic unit elongation index 5% of space flight and aviation structural part, but axial and very little perpendicular to the power difference in hot pressing axially along hot pressing.After crimp, significantly improve along the intensity in the direction of extrusion and plasticity, unit elongation exceedes 5%, but less perpendicular to the intensity in the direction of extrusion and plasticity lifting amplitude, the mechanical property gap on both direction is larger.Finally by forging deformation, although with bar along compared with the performance in the direction of extrusion, intensity and plasticity slightly decline, the intensity of material all directions and plasticity, in same level, have arrived homogeneous, the isotropic target of material internal.
Fig. 1 has provided 15vol.%SiC
pthe metallographic microstructure of/2009Al matrix material.Fig. 1 (a) and (b) be matrix material hot pressing billet along hot pressing direction with perpendicular to the metallographic microstructure of hot pressing direction, the microtexture on both direction is basically identical.In figure, white portion is aluminium powder form, and gray area is SiC particle, in matrix material without hole, the defect such as loose.Aluminium powder form is all spherical in shape, the gap of SiC particle agglomeration between aluminium powder form, skewness.After crimp, having there is distortion significantly in aluminium powder form, is squeezed into ribbon, and as shown in Fig. 1 (c), the SiC particle that size is less progresses in the aluminum substrate after distortion, also presents obvious zonal arrangement.Because aluminium powder form is elongated, diameter diminishes, become evenly in the SiC size distribution perpendicular in the direction of extrusion, as shown in Fig. 1 (d), but with have obvious difference along the tissue in the direction of extrusion.Finally by crossing forging deformation, in former bar, banded structure and point range of distribution are destroyed, reaching unanimity along forging direction with perpendicular to the microtexture of forging in direction, as Fig. 1 (e) with (f), SiC particle all disperse is evenly distributed in aluminum substrate, and the mechanical property of both direction, in same level, has finally obtained isotropy and high-strength and high ductility particle enhanced aluminum-based composite material.
Table 1 15vol.%SiC
pthe mechanical property of/2009Al matrix material
Table 2 25vol.%SiC
pthe mechanical property of/2009Al matrix material
Claims (5)
1. isotropy and a high-strength and high ductility particle enhanced aluminum-based composite material, be made up of reinforcement particle and Al alloy powder, it is characterized in that,
(1) the spatially disperse of reinforcement particle is uniformly distributed in alloy matrix aluminum, and forms good interface with matrix and be combined;
(2) size range of reinforcement particle is 1 ~ 25 μ m;
(3) volume percent of reinforcement particle is 5 ~ 30%;
(4) size range of Al alloy powder is 5 ~ 60 μ m;
That the processing mode manufacture that adopts reinforcement particle and Al alloy powder batch mixing, vacuum hotpressing to be configured as billet, is hot extruded into bar and high temperature forging or hot rolling forms.
2. isotropy according to claim 1 and high-strength and high ductility particle enhanced aluminum-based composite material, is characterized in that, described reinforcement particle is Al
2o
3any one in (aluminum oxide), SiC (silicon carbide) and AlN (aluminium nitride); Alloy matrix aluminum is any one alloy in duralumin (2 × × ×).
3. a method of manufacturing isotropy and high-strength and high ductility particle enhanced aluminum-based composite material, is characterized in that, the method comprises the steps:
(1) matrix alloy of the reinforcement particle that is 5 ~ 30% according to volumn concentration in designed matrix material and volumn concentration 70 ~ 95%, calculates the two required weight separately;
(2) required reinforcement particle, Al alloy powder and steel ball are joined in the mixing machine of standard machinery mixer, carry out mechanical batch mixing;
(3) composite powder making is packed in No. 45 steel die, then vacuum hotpressing is configured as billet, and hot pressing temperature is 600 ~ 650 ℃, and vacuum tightness is 1 ~ 8 × 10
-3pa, pressure is 50 ~ 100MPa;
(4) matrix material hot pressing billet is carried out to hot extrusion, extrusion temperature is 400 ~ 450 ℃, and extrusion ratio is 10 ~ 20:1, and extrusion speed is 0.1 ~ 5mm/s;
(5) matrix material extruded bars is divided into the bar that length is 500 ~ 1200mm, partition tools can adopt Wire EDM, band saw or disc saw;
(6) the matrix material bar that is 500 ~ 1200mm by length carries out high temperature forging or hot rolling, forging or rolling temperature are 400 ~ 450 ℃, total deformation >60%, single pass heavy deformation should be <45%, every time need carry out the high temperature anneal, and annealing process is: 400 ~ 450 ℃ of insulation 2 ~ 4h.
4. according to the preparation method of the isotropy described in claim 3 and high-strength and high ductility particle enhanced aluminum-based composite material, it is characterized in that, the steel ball in step (2) is high-carbon steel ball, and its steel ball size is Ф 10 ~ 15mm.
5. according to the preparation method of the isotropy described in claim 3 and high-strength and high ductility particle enhanced aluminum-based composite material, it is characterized in that, in step (2), mixing time is 20 ~ 30h, and ball material weight ratio is 1:1, and mixer rotating speed is 25 ~ 30rpm.
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Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS63199839A (en) * | 1987-02-13 | 1988-08-18 | Sumitomo Electric Ind Ltd | Wear-resistant aluminum-alloy composite material |
| CN1422970A (en) * | 2001-12-06 | 2003-06-11 | 北京有色金属研究总院 | Particle reinforced aluminium-based composite material and manufacture method thereof |
| CN1510153A (en) * | 2002-12-26 | 2004-07-07 | 北京有色金属研究总院 | High strength and ductility particle reinforced aluminium base composite material and preparing method thereof |
| CN101708527A (en) * | 2009-12-10 | 2010-05-19 | 北京有色金属研究总院 | Forging technology of particle-reinforced aluminum-based composite material |
| CN102534289A (en) * | 2010-12-09 | 2012-07-04 | 北京有色金属研究总院 | Extrusion process of granule-reinforced aluminum-based composite material |
-
2012
- 2012-12-12 CN CN201210535064.2A patent/CN103866165A/en active Pending
Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS63199839A (en) * | 1987-02-13 | 1988-08-18 | Sumitomo Electric Ind Ltd | Wear-resistant aluminum-alloy composite material |
| CN1422970A (en) * | 2001-12-06 | 2003-06-11 | 北京有色金属研究总院 | Particle reinforced aluminium-based composite material and manufacture method thereof |
| CN1510153A (en) * | 2002-12-26 | 2004-07-07 | 北京有色金属研究总院 | High strength and ductility particle reinforced aluminium base composite material and preparing method thereof |
| CN101708527A (en) * | 2009-12-10 | 2010-05-19 | 北京有色金属研究总院 | Forging technology of particle-reinforced aluminum-based composite material |
| CN102534289A (en) * | 2010-12-09 | 2012-07-04 | 北京有色金属研究总院 | Extrusion process of granule-reinforced aluminum-based composite material |
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Application publication date: 20140618 |